Influence of phase transformation on the work hardening characteristics of Pb-(1-3)wt.%Sb alloys

IOSR Journal of Mechanical and Civil Engineering (IOSR-JMCE) e-issn: 2278-1684,p-ISSN: 232-334X, Volume 12, Issue 6 Ver. V (Nov. - Dec. 215), PP 53-65 www.iosrjournals.org Influence of phase transformation on the work hardening characteristics of Pb-(1-3)wt.%Sb alloys Gh. Mohammed 1, S. El-Gamal* 1, A. S. Mahmoud 2, R. H. Nada 2 and A.M. Abd El-Khalek 2 1 Physics Department, Faculty of Science, Northern Border University, Arar, 91431, KSA, permanent address; Physics Department, Faculty of Education, Ain Shams University, Cairo, 11747, Egypt. 2 Physics Department, Faculty of Education, Ain Shams University, Cairo, 11747, Egypt *Corresponding author. Tel.: 966 567414468. E-mail address: samyelgamal@gmail.com Abstract: This study focuses on the effect of phase transformation on the work hardening characteristics of Pb- (1-3)wt.%Sb alloys either quenched (type I) or slowly cooled samples (type II) at different ageing temperature (T a ). Three work hardening characteristics were studied which are; the coefficient of work hardening p, yield stress σ y and fracture stress σ f. It was found that; these parameters of both types of samples decrease with increasing T a, showing two stages around the transformation temperature which changes with the Sb addition and equal to 453 K for 1wt.%Sb, 483 K for 2wt.%Sb and 513 K for 3wt.%Sb. The values of these parameters of type I samples were higher than type II samples. The fracture strain ε f, the strain at the fracture point, increases with increasing T a showing two stages also. The dislocation slip distance, L, increases as T a increases. The magnitude of the variation of all these parameters point to two fracture mechanisms activated with.11 and.39 ev for 1wt.%Sb,.15 and.49 ev for 2wt.%Sb,.2 and.65 ev for 3wt.%Sb for type I samples and equal.21 and.52 ev for 1wt.%Sb,.17 and.56 ev for 2wt.%Sb,.16 and.63 ev for 3wt.%Sb for type II for both first and second stages, respectively. The microstructure of the samples under investigation has been examined after stress-strain measurements by scanning electron microscope. Keywords: Work hardening characteristics, Ageing temperature, Pb-Sb alloys, Mechanical characterization I. Introduction Lead is very soft and ductile so it is normally used commercially as lead alloys [1]. Lead alloys had become established by the end of the first half of the twentieth century [2]. Antimony, tin, arsenic, and calcium are the most common alloying elements [3]. The addition of Antimony, in particular, enhances the alloy hardness greatly and lowers the casting temperature and minimizes the contraction during freezing. Indeed, such addition plays a vital role in increasing the resistance to compressive impact and wear [4]. Also, it increases the conductive properties [5]. In fact, such addition produces a significant segregation at grain boundaries and a high concentration of alloying vacancies which should modify the viscous flow processes along the grain boundaries [6]. Antimony contents in lead-antimony alloys can range from.5 to 25%, but they are usually about 2-5% [1]. Lead- antimony alloys are considered as an important material in industrial applications for their use as the best stable material for battery grids in accumulator manufacturing [7, 8] because of the properties of Pb-Sb alloys, mentioned lately. It should be noted that, these alloys are very well hardened by continuous precipitation, whereas lead tin alloys present a discontinuous precipitation with a weak hardening effect [9]. It is noted that, the choice of the suitable heat treatment plays an important role in enhancing the mechanical properties of the metallic materials to achieve more applications in industry and this topic attracts more and more investigators [-15]. Pb-Sb alloy consists of Pb-rich phase and some amounts of Sb-rich phase this is according to its phase diagram [16]. It was reported that, Sb-rich phase has always formed at the boundaries of Pb-rich phase [7] and the solid solubility of Sb in Pb increases as the heating temperature increases up to transformation temperature. The process of ageing of the super-saturated solid solution of this alloy leads to the formation of more β-phase. The thorough surveying of the literature has revealed that; some investigators were interested in studying the corrosion resistance and electrochemical behavior of the Pb-Sb alloys [2, 17] while others studied their structure and mechanical properties by changing the deformation temperature [18, 19] or with adding of tin [18]. As was noticed, little attention has been given to the topic of effect of ageing temperature (423-543 K) on the work hardening characteristics of Pb-(1-3)wt.%Sb alloys and this represents a gap. So the aim of the present work is to try to fill this gap. DOI:.979/1684-12655365 www.iosrjournals.org 53 Page

II. Experimental procedure 2.1 Alloy preparation and heat treatment Pb-(1-3)wt.%Sb alloys were prepared from high purity Pb and Sb (99.99%) by melting a mixture of the appropriate weights under vacuum in a high purity graphite crucible, in a high frequency induction furnace. The obtained ingot was homogenized at 553 K for 8 h then cold drawn into two forms; wires of diameter.6 mm and sheets of thickness.4 mm. Chemical analysis revealed that sample composition is very close to the alloy compositions required. The samples were divided into two parts, one of them were quenched in water at RT (type I) while the remaining (other) part were slowly cooled (type II). Ageing of the samples (wires and sheets) were performed in the temperature range; 423-483K, 453-513K and 483-543 K for Pb-1wt.%Sb, 2wt.%Sb and 3wt. %Sb alloys, respectively, with accuracy ±2 K, at an interval of K and the time of ageing was 1 hr. 2.2 Measurements 2.2.1 Tensile test One of the most important tests to investigate the material's mechanical properties is the tensile test. This test was performed using a computerized locally made tensile testing machine. More details about this machine were described elsewhere [2]. All samples were stretched with a constant strain rate of 1.2-3 s -1 at room temperature (3 K) up to fracture. 2.2.2 Microstructure examination The microstructure of Pb-Sb alloys were investigated using scanning electron microscope (SEM) (JEOL, JSM-54) and energy dispersive X-ray spectroscopy (EDS). Using different techniques helped us to investigate the microstructure precisely. III. Results 3.1 Tensile properties The engineering stress-strain curves at different T a for both types of Pb-(1-3)wt.%Sb alloys are shown in Figs. (1-3). It was found that, the stress-strain curves vary with changing T a for the both types of the samples. Figs. (4-6) show the dependence of the work hardening parameters ( p, σ y and σ f ) on T a. Where σ y is called the yield stress, σ f is the fracture stress and p is the work-hardening coefficient, which could be calculated from the parabolic part of stress-strain curves (Figs. (1-3)) by using the following equation; It was found that, the three parameters decrease as the ageing temperature increases for the both types of the samples and such decrease occurred in two distinguished stages. The first one extends to temperatures up to 453 K for 1wt.% Sb, 483 K for 2wt.% Sb and 513 K for 3wt.% Sb and the second stage extends to a higher range above 453 K, 483 K and 513 K. The values of p, σ y and σ f for samples of type I are higher than those of type II. The fracture strain ε f (the strain corresponding to the fracture point in the stress-strain curves) as a function of T a is shown in Fig. 7. It is clear that ε f increases as the ageing temperatures increase and showing two stages for the two types of alloy samples. Also, the value of ε f for type I samples were found to be less than type II at all the applied temperatures. The dislocation slip distance L is one of the important parameters in the field of tensile properties of materials [21]. Its values could be found by applying Mott s work hardening model [22]. The model predicts that the coefficient of work hardening is given by the equation: where L is the distance slipped by the moving dislocation, G is the shear modulus for Pb alloy (G=4.3x 4 MPa), and b is the Burgers vector (b = 3.5x - m) [23]. The dependence of L on T a for both types of samples is depicted in figure 8. It is clear that, increasing T a resulted in increasing L. 2-Structural properties It is well known that, investigating the microstructure of different Pb-(1-3)wt.%Sb alloys plays a vital role in determining and predicting the mechanical response. In the present study, the evaluation of the microstructure changes due to the aging temperature under different conditions was performed by using SEM and EDS investigations. Figure 9 shows SEM micrographs of the Pb-2wt.% Sb quenched samples (type I) aged for 1h at the temperatures 463,483 and 513K. As observed, there are two phases, dark phase and white phase, the white phase was detected to be Sb-rich phase embedded in dark phase, which is the Pb-matrix and this was confirmed by EDS investigation. Also, the Sb-rich phase in Pb-matrix decrease with increasing ageing temperature. (2) (1) DOI:.979/1684-12655365 www.iosrjournals.org 54 Page

IV. Discussion The stress-strain curves in the present work were considered as raw experimental data and hence it is more suitable to discuss the parameters extracted from these curves other than discussing the curves themselves. The decrease in p, σ y and σ f in the first stage (see Figs. (4-6)) could be attributed to the amount of the second phase (β-phase or Sb-rich phase) and its corresponding diffusivity with the matrix (Pb) which controls the dislocation mobility at the inter-phase boundaries [24]. This continues until the transformation temperature, which is 453 K, 483 K and 513 K for 1, 2 and 3wt. % Sb respectively. But, in the second stage, i.e., above transformation temperature, the β-phase dissolves completely and disappears [25] and this result in an intensive decrease in the work hardening parameters which could be due to the relaxation of dislocations at the fronts of the pileups at grain boundaries [26]. This process might be associated with dislocation annihilation by increased thermal agitation [18]. The above explanation was confirmed by SEM micrographs (see Fig. 9) for the sample Pb 2wt.% Sb, as an example, at different ageing temperatures 463, 483 and 513 K. From these micrographs, the solubility of Sb-rich phase in Pb-matrix increases until the transformation temperature, 483 K, and after that the Sb-rich phase disappears. On the other hand, ε f increases as T a increases (see Fig. 7) because in the first stage the solubility of Sb in Pb increases, so the motion of dislocations enhanced as a result of the decrease in the percent of Sb-rich phase. In the second stage the materials became more ductile due to the rearrangement of the dislocations [27]. The higher values of p, σ y and σ f for type I samples compared with type II is due to the more tangling in dislocations occurred in type I samples because of the quenching process [28] which obstacle the movement of Sb-rich phase. But for type II samples the dislocation motion is easier. The higher values of ε f of the type II samples than type I (see Fig. 7) is due to the relaxation of alloy as a result of some degree of dislocation annihilation which accelerate the solubility of β-phase in the matrix, reduces the hardness and consequently increases the ductility, i.e., ε f increases. For type I samples, ε f is lower because the sample became harder due to the quenching process. Increasing the Sb content, the work hardening parameters increases while ε f decreases this is because the addition of Sb hardens the alloy. The increase in L as T a increases (see Fig. 8) could be due to the relaxation of dislocation heads of the pileups at the phases existed in the Pb-matrix. This relaxation is accompanied by escaping of dislocations from these pileups by the cross-slipping process as a result of the thermal agitation. Finally, the dislocations will move through longer slip distances L. The activation energies of the operating mechanisms in both types I and II are determined from the slopes of the straight lines of the relation between Ln (σ f ) and /T as shown in Fig. according to the Arrhenius s equation; σ f =A exp. (Q/RT) (3) where A is a constant, Q is the activation energy in ev and R is the gas constant. The values of the activation energies were represented in Table (1). It is clear that, the values of Q in type II samples are higher than that of type I. For all the samples, Q values in region II are higher. These values indicate that the operating mechanism may be a dislocation intersection [8, 29] and diffusion of Sb through Pb-Sb boundaries [8] in the low temperature range. While in the high temperature range, grain boundary sliding is the principal mechanism [7, 8]. V. Conclusion The effect of phase transformation on the work hardening characteristics of Pb-(1-3)wt.%Sb alloys either quenched (type I) or slowly cooled samples(type II) at different ageing temperature (T a ) was studied. The coefficient of work hardening p, yield stress σ y and fracture stress σ f were found. They decrease with increasing T a in two stages around the transformation temperature. The transformation temperature changes with the addition of Sb and equal 453 K for 1wt.%Sb, 483 K for 2wt.%Sb and 513 K for 3wt.%Sb. The values of these parameters of the type I samples were higher than those of type II. The fracture strain ε f, the strain at the fracture point, increases with increasing T a showing two stages also. The dislocation slip distance, L, increases as T a increases. The operating mechanism may be dislocation intersection and diffusion of Sb through Pb-Sb boundaries in the low temperature range and changed to the grain boundary sliding in the high temperature range. References [1] Davis J R, Alloying: Understanding the Basics, ASM International (21) [2] Ghasemi Z and Tizpa A, Int. J. Electrochem. Sci. 3 (28) 727. [3] Morrison R D and Murphy B L, Environmental Forensics: Contaminant Specific Guide, Academic Press (25). [4] Metikos-Hukovic M, Babic R and Brinic S, J Power Sources 64 (1997) 13. [5] Laitinen T, Salmi K, Sundholm G, Monghova B, and Pavlova D, Electrochimica Acta 36(3-4), (1991) 65. [6] Elsukova T F, Panin V E, Veselova D V and Veselov Yu G, Russian Phys J 3 (11) (1988) 923. [7] Al-Ganainy G S, Mostafa M T and Nagy M R, Phys. Stat. Sol. A 165 (1998) 185. [8] Al-Ganainy G S, Mostafa M T and Abd El-Salam F, Physica B 348 (24) 242. DOI:.979/1684-12655365 www.iosrjournals.org 55 Page

Stress, (MPa) [9] Hilger J P, J. Power Sources 53 (1995) 45. [] El-Gamal S and Mohammed Gh, Radiat. Phys. Chem. 99 (214) 68-73. [11] El-Gamal S and Mohammed Gh, J Iron Steel Res Int, 23 (7) (216), accepted to be published. [12] Abdel-Hady E E, Ashry A, Ismail H, El-Gamal S, Appl. Surf. Sci. 252 (26) 3297. [13] El-Gamal S, Radiat. Phys. Chem. 9 (213) 32. [14] Saad G, Soliman H N, Fawzy A, Mohammed Gh, Arab J Nucl Sci Appl. 44 (211) 313. [15] Habib N, Mohammed Gh, Saad G, Fawzy A, Arab J Nucl Sci Appl. 41(1) (28) 215. [16] Hansen M, Constitution of binary alloys 2 ed., McGraw-Hill, London (1958) [17] Ghasemi Z and Tizpa A, Int. J. Electrochem. Sci. 2 (27) 7. [18] Abd El-Khalek A M and Nada R H, Physica B 328 (23) 393. [19] Fawzy A, Awadallah A S M, Sobhy M, and Saad G, Physica B 355 (25) 286. [2] Saad G, Fayek S A, Fawzy A, Soliman H N and Mohammed Gh, Mat. Sci. Eng. A-Struct. 527 (2) 94. [21] Shaha S K, Czerwinski F, Chen D L and Kasprzak W, Mater Sci Tech 31(1) (215) 63. [22] Mott N F, Dislocations and Mechanical Properties of Crystals, Wiley, New York, (1957). [23] Kittel C, Introduction to Solid State Physics, Wiley Eastern Ltd., New Delhi, (1984). [24] Lukac P, Malygin G A and Vladimirova A G V, Czech. J. Phys. B 35(3) (1985) 318. [25] El-Sayed M M, Abd El-Salam F, Abd El-Haseeb R and Nagy M R, Phys. Stat. Sol. A 144 (1994) 329. [26] Soer W A, Interactions between dislocations and grain boundaries, PhD thesis series, 26 [27] Reardon C, Metallurgy for the Non-Metallurgist 2ed, ASM International, (211). [28] Lim N S, Bang C W, Das S, Jin H W, Ayer R and Park C G, Met. Mater. Int. 18(1) (212) 87. [29] El-Sayed M M, Abd El-Salam F, Abd El-Haseeb R, Phys. Stat. Sol. A 147(2) (1995) 41. Figure Captions Fig. (1): Stress strain curves of both types of Pb 1wt.%Sb alloy. Fig. (2): Stress strain curves of both types of Pb 2wt.%Sb alloy. Fig. (3): Stress strain curves of both types of Pb 3wt.%Sb alloy. Fig. (4): The dependence of work-hardening coefficient, p on the ageing temperature for both types of Pb 1-3wt.% Sb alloys. Fig. (5): The dependence of yield stress, σ y on the ageing temperature for both types of Pb 1-3wt.% Sb alloys Fig. (6): The fracture stress, σ f as a function of ageing temperature for both types of Pb 1-3wt.% Sb alloys Fig. (7): The fracture strain, f as a function of ageing temperature for both types of Pb 1-3wt.% Sb alloys Fig. (8): Temperature dependence of slip distance, L for both types of Pb 1-3wt.% Sb alloys Fig. (9): SEM micrographs of the quenched samples (2wt.% Sb) at different ageing temperatures Fig. (): The relation between Ln (σ f ) and /T of both types of Pb 1-3wt.% Sb alloys Table (1): The values of the activation energies for both types of Pb 1-3wt.% Sb alloys Region I Region II Type I Type II Type I Type II.11.12.39.52.15.17.49.56.2.16.65.63 22 2 18 16 14 12 Pb-1wt.%Sb (type I) 423K 433K 443K 453K 463K 473K 483K 8 6 4 2..5..15.2.25.3.35.4 Strain, DOI:.979/1684-12655365 www.iosrjournals.org 56 Page

Stress, (MPa) Stress, (MPa) 22 2 18 16 14 12 Pb-1wt.%Sb (type II) 423K 433K 443K 453K 463K 473K 483K 8 6 4 2..5..15.2.25.3.35.4 Strain, Fig. (1): Stress strain curves of both types of Pb 1wt% Sb alloy. 3 Pb-2wt.%Sb (type I) 25 2 15 453K 463K 473K 483K 493K 53K 513K 5..5..15.2.25.3 Strain, DOI:.979/1684-12655365 www.iosrjournals.org 57 Page

Stress, (MPa) Stress, (MPa) 3 Pb-2wt.%Sb (type II) 25 2 15 453K 463K 473K 483K 493K 53K 513K 5..5..15.2.25.3 Strain, Fig. (2): Stress strain curves of both types of Pb 2wt% Sb alloy. 4 35 3 25 2 Pb-3wt.%Sb (type I) 483K 493K 53K 513K 523K 533K 543K 15 5..3.6.9.12.15.18 Strain, DOI:.979/1684-12655365 www.iosrjournals.org 58 Page

Stress, (MPa) 4 35 3 25 2 Pb-3wt.%Sb (type II) 483K 493K 53K 513K 523K 533K 543K 15 5..3.6.9.12.15.18 Strain, Fig. (3): Stress strain curves of both types of Pb 3wt% Sb alloy. Work-Hardening Coefficient, p (MPa) 2 5 4 Type I 3 2 DOI:.979/1684-12655365 www.iosrjournals.org 59 Page

Yield Stress, y (MPa) 4 Type II Work-Hardening Coefficient, p (MPa) 2 3 2 Fig. (4): The dependence of work-hardening coefficient, p on the ageing temperature for both types of Pb 1-3wt% Sb alloys. 2 18 16 14 12 8 6 4 2 Type I DOI:.979/1684-12655365 www.iosrjournals.org 6 Page

Fracture Stress, f (MPa) Yield Stress, y (MPa) 14 12 Type II 8 6 4 2 Fig. (5): The dependence of yield stress, σ y on the ageing temperature for both types of Pb 1-3wt% Sb alloys 4 35 3 Type I 25 2 15 DOI:.979/1684-12655365 www.iosrjournals.org 61 Page

Fracture Stress, f (MPa) 3 25 2 Type II 15 5 Fig. (6): The fracture stress, σ f as a function of ageing temperature for both types of Pb 1-3wt% Sb alloys.35.3.25 Type I Fracture Strain, f.2.15..5. DOI:.979/1684-12655365 www.iosrjournals.org 62 Page

.45 Slip distance, L (m).4.35 Type II Fracture Strain, f.3.25.2.15..5. Fig. (7): The fracture strain, f as a function of ageing temperature for both types of Pb 1-3wt% Sb alloys 6.x -5 5.x -5 Type I 4.x -5 3.x -5 2.x -5 1.x -5. DOI:.979/1684-12655365 www.iosrjournals.org 63 Page

Slip distance, L (m) 4.x -4 Type II 3.x -4 2.x -4 1.x -4. Fig. (8): Temperature dependence of slip distance, L for both types of Pb 1-3wt% Sb alloys 3 µm 3 µm Fig. (9): SEM micrographs of the quenched samples (2wt.% Sb) at different ageing temperatures. DOI:.979/1684-12655365 www.iosrjournals.org 64 Page

Ln ( f ) Ln ( f ) 3.5 type I 3. 2.5 1.8 1.9 2. 2.1 2.2 2.3 2.4 /T(K) 3.4 3.2 3. type II 2.8 2.6 2.4 2.2 2. 1.8 1.9 2. 2.1 2.2 2.3 2.4 /T(K) Fig. (): The relation between Ln (σ f ) and /T of both types of Pb 1-3wt% Sb alloys. DOI:.979/1684-12655365 www.iosrjournals.org 65 Page